There is provided a Ti—Al-based alloy ingot having ductility at room temperature, in which the Ti—Al-based ingot has a lamellar structure in which α2 phases and γ phases are arranged sequentially and regularly, and a thickness ratio γ/α2 of the γ phase to the α2 phase is equal to or more than 2. There is also provided a Ti—Al-based alloy ingot having ductility at room temperature, in which the Ti—Al-based alloy ingot has a lamellar structure in which α2 phases and γ phases are arranged sequentially and regularly, the γ phase has a thickness of 100 nm to 200 nm, and the α2 phase has a thickness of 100 nm or less.
|
1. A Ti—Al-based alloy ingot having ductility at room temperature, wherein the Ti—Al-based ingot has a lamellar structure in which α2 phases and γ phases are arranged sequentially and regularly, and a thickness ratio γ/α2 of the γ phase to the α2 phase is equal to or more than 2, and
wherein the Ti—Al-based alloy ingot includes 46 at % of aluminum (Al), 6 at % of niobium (Nb), 0.5 at % of tungsten (W), 0.5 at % of chromium (Cr), 0.3 at % of silicon (Si), 0.1 at % of carbon (C), and titanium (Ti) as a remainder, wherein the Ti—Al-based alloy ingot has a tensile strength of 640 mpa or more.
4. A Ti—Al-based alloy ingot having ductility at room temperature, wherein the Ti—Al-based alloy ingot has a lamellar structure in which α2 phases and γ phases are arranged sequentially and regularly, the γ phase has a thickness of 100 nm to 200 nm, and the α2 phase has a thickness of 100 nm or less, and
wherein the Ti—Al-based alloy ingot includes 44 at % of aluminum (Al), 6 at % of niobium (Nb), 0.5 at % of tungsten (W), 0.5 at % of chromium (Cr), 0.3 at % of silicon (Si), 0.1 at % of carbon (C), and titanium (Ti) as a remainder, wherein the Ti—Al-based alloy ingot has a tensile strength of 640 mpa or more.
5. A Ti—Al-based alloy ingot having ductility at room temperature in a casting state prior to a subsequent heat treatment, wherein the Ti—Al-based ingot has a lamellar structure in which α2 phases and γ phases are arranged sequentially and regularly, a thickness ratio γ/α2 of the γ phase to the α2 phase is equal to or more than 2, and
wherein the Ti—Al-based alloy ingot includes 44-46 at % of aluminum (Al), 6 at % of niobium (Nb), 0.5 at % of tungsten (W), 0.5 at % of chromium (Cr), 0.3 at % of silicon (Si), 0.1 at % of carbon (C), and titanium (Ti) as a remainder, wherein the Ti—Al-based alloy ingot has a tensile strength of 640 mpa or more.
2. The Ti—Al-based alloy ingot of claim of
3. The Ti—Al-based alloy ingot of claim of
7. The Ti—Al-based alloy ingot of
8. The Ti—Al-based alloy ingot of
|
This application claims the priority of Korean Patent Application No. 10-2013-0056313 filed on May 20, 2013, in the Korean Intellectual Property Office, the disclosure of which is incorporated herein by reference.
Technical Field
The present disclosure relates to a Ti—Al-based alloy ingot having ductility at room temperature, and more particularly, to a Ti—Al-based alloy ingot having ductility at room temperature, which has a lamellar structure in which α2 phases and γ phases are arranged subsequently and regularly and has ductility at room temperature in a casting state where the subsequent heat treatment is not performed by controlling a width of the α2 phase, a width of the γ phase and a ratio of α2/γ.
Description of the Related Art
A Ti—Al-based alloy is a kind of intermetallic compounds that have been spotlighted as an advanced light-weight heat-resistant material, and is a two-phase alloy including about 10% of Ti3Al.
An ingot having a two-phase lamellar structure of TiAl(γ)+Ti3Al(α2) is produced by a typical melt solidification method.
Due to superiority in fracture toughness, fatigue strength and creep strength, a lamella structure of the TiAl enables the TiAl to exhibit characteristics useful to be practicalized as a light-weight high-temperature material, but it is difficult for the TiAl to be used as a casting material because of insufficient ductility at room temperature.
Such insufficient ductility is primarily caused by delamination occurring at a lamellar boundary when stress is vertically applied to the boundary.
Accordingly, by reducing sizes of crystal grains and adding beta and gamma phases having relatively excellent ductility as compared with the lamellar structure, there have been efforts to improve strength and ductility of the TiAl as well as high-temperature characteristics.
In the related art for producing the TiAl alloy having a lamellar structure including beta and gamma phases, a Ti—(41˜45)Al—(3˜5)Nb—(Mo,V)—(B,C)-based alloy is used (H. Z. Niu et al., intermetallics 21 (2012) 97 and T. Sawatzky, Y. W. Kim et al., Materials Science Forum, 654-656 (2010) 500)).
Further, U.S. Pat. No. 4,294,615 discloses a technology of improving ductility of a TiAl by adding vanadium (V) to a gamma TiAl matrix, and U.S. Pat. No. 4,842,820 discloses a technology of improving strength and ductility of a TiAl by adding Boron (B).
In addition, U.S. Pat. Nos. 4,842,819 and 4,879,092 disclose a technology of improving ductility of a TiAl by adding chrome (Cr) and a technology of improving ductility and oxidation resistance of a TiAl by simultaneously adding chrome and niobium, respectively.
Disadvantageously, in the aforementioned related arts, since hot processing such as hot forging, rapid solidification, and hot extrusion are performed on the TiAl, it is difficult to simply predict from a result of such hot processing whether or not characteristics of a casting body are improved.
Moreover, since mechanical characteristics are tested through a high-temperature measurement or a bending test is performed, it is difficult to understand tensile properties at room temperature.
In order to solve the above-described problems, an aspect of the present disclosure provides a Ti—Al-based alloy ingot having ductility at room temperature in a casting state.
An aspect of the present disclosure also provides a Ti—Al-based alloy ingot having ductility at room temperature, which has a lamellar structure in which α2 phases and γ phases are arranged subsequently and regularly and has ductility at room temperature in a casting state where the subsequent heat treatment is not performed by controlling a width of the α2 phase, a width of the γ phase and a ratio of α2/γ.
An aspect of the present disclosure also provides a Ti—Al-based alloy ingot having ductility at room temperature with which it is possible to improve high-temperature characteristics as well as room-temperature characteristics.
According to an aspect of the present disclosure, there is provided a Ti—Al-based alloy ingot having ductility at room temperature. The Ti—Al-based ingot may have a lamellar structure in which α2 phases and γ phases are arranged sequentially and regularly, and a thickness ratio γ/α2 of the γ phase to the α2 phase may be equal to or more than 2.
According to another aspect of the present disclosure, there is provided a Ti—Al-based alloy ingot having ductility at room temperature. The Ti—Al-based alloy ingot may have a lamellar structure in which α2 phases and γ phases are arranged sequentially and regularly, the γ phase may have a thickness of 100 nm to 200 nm, and the α2 phase may have a thickness of 100 nm or less.
The Ti—Al-based alloy ingot may include 44 to 46 at % of aluminum (Al), 6 at % of niobium (Nb), 1.0 at % of creep-property improver, 1.0 at % of softening-resistant improver, and titanium (Ti) as a remainder.
The creep-property improver may include carbon (C) and silicon (Si).
The softening-resistant improver may include tungsten (W) and chrome (Cr).
The Ti—Al-based alloy ingot may have a tensile strength of 640 MPa or more.
The above and other aspects, features and other advantages of the present disclosure will be more clearly understood from the following detailed description taken in conjunction with the accompanying drawings, in which:
As required, detailed embodiments are disclosed herein. However, it is to be understood that the disclosed embodiments are merely exemplary. Additionally, the features of various implementing embodiments may be combined to form further embodiments. The figures are not necessarily to scale and features may be exaggerated or minimized to show details of particular components. Therefore, specific structural and functional details disclosed herein are not to be interpreted as limiting, but merely as a representative basis for teaching one skilled in the art.
As set forth above, according to embodiments of the present disclosure, there is a merit that it is possible to provide a Ti—Al-based alloy ingot having ductility at room temperature in a casting state, which has a lamellar structure in which α2 phases and γ phases are arranged subsequently and regularly.
Further, there is also a merit that the Ti—Al-based alloy ingot has ductility at room temperature in a casting state where the subsequent heat treatment is not performed by controlling a width of the α2 phase, a width of the γ phase and a ratio of α2/γ.
Furthermore, there is also a merit that high-temperature characteristics are improved as well as high-temperature characteristics.
Hereinafter, a Ti—Al-based alloy ingot having ductility at room temperature according to the present disclosure will be described with reference to
Before the description thereof, all terms and words used in the specifications and claims are not interpreted as the meaning generally used in the dictionary, but should be interpreted as the meaning and concept coincident with the technological sprit of the present disclosure on the basis of a fundamental rule that an inventor can suitably define the concept of corresponding terms to describe his or her disclosure using the best method.
Accordingly, embodiments described in the specifications and configurations illustrated in the drawings are merely a preferred embodiment, and do not wholly represent the technical sprit of the present disclosure. Therefore, it should be appreciated that various modifications and equivalents to these embodiments are possible at the time of filing the present application.
As shown in the drawings, the Ti—Al-based alloy ingot (hereinafter, referred to as a Ti—Al alloy 10) having ductility at room temperature according to the present disclosure is produced by a solidification casting method on the basis of compositions having an atom ratio of components represented in Embodiment 1 and Embodiment 2 shown in
More specifically, when the subsequent process such as heat treatment is performed on the Ti—Al alloy 10, it is obvious that mechanical characteristics such as hardness, softening resistance and creep properties of the Ti—Al alloy are improved. However, the hardness and tensile strength of button-shaped Ti—Al alloys according to Embodiments of the present disclosure, which have diameters of 60 mm and are produced by the solidification casting method, are tested and compared with Ti—Al alloys according to Comparative Examples.
At this time, a Ti—Al alloy according to Comparative Example 1 is produced based on a TiAl heat-resistant alloy composition described in Japanese Patent Laid-Open Publication Nos. H10-220236 and H10-193087 filed by Daido Steel Co., Ltd in Japan, and a Ti—Al alloy according to Comparative Example 2 is produced based on a TiAl alloy composition described in Korean Patent No. 10-1261885.
Embodiments of the present disclosure are divided into Embodiment 1 and Embodiment 2 according to a difference in composition of aluminum (Al).
That is, the Ti—Al alloys according to Embodiments include 6 at % of niobium (Nb), 1.0 at % of softening-resistant improver, 1.0 at % of creep-property improver, and titanium (Ti) as a remainder, and have slightly different aluminum (Al) compositions of 44 at % and 46 at %, respectively.
At this time, the creep-property improver includes carbon (C) and silicon (Si), and the softening-resistant improver includes tungsten (W) and chrome (Cr). Further, the Ti—Al alloys according to Embodiments have a tensile strength of 640 MPa or more in a state where the subsequent process such as heat treatment is not performed.
Next, microstructures of the Ti—Al alloy according to Embodiment 1 of the present disclosure and the Ti—Al alloys according to Comparative Examples 1 and 2 are compared with reference to
First, as shown in
Further, as shown in
Furthermore, it can be seen that the Ti—Al alloy according to Embodiment 1 has a lamellar structure, a thickness ratio γ/α2 of the γ phase to the α2 phase is equal to or more than 2, and a thickness of the α2 phase is thinner than a thickness of the γ phase.
Namely, the α2 phase has a thickness of 100 nm or less, whereas the γ phase has a thickness of 100 nm to 200 nm. Thus, the α2 phase has a thickness relatively thinner than that of the γ phase, and the α2 phases and the γ phases are alternately arranged in a lamellar structure.
In contrast, as shown in
Moreover, as shown in the lowest photograph of
When characteristics of the Ti—Al alloys according to Embodiments shown in
Here, the Ti—Al alloy according to Embodiment 1 of the present disclosure has tensile strength far superior to the Ti—Al alloy according to Comparative Examples.
The above-mentioned experiment results are obtained by measuring the Ti—Al alloy according to Embodiment 1, which is produced by the solidification casting method based on the compositions represented in
Accordingly, when the subsequent processes are further performed on the Ti—Al alloy, it is expected that such characteristics can be more improved. Thus, as shown in
As shown in
Accordingly, the Ti—Al alloys according to Embodiments have high oxidation resistance and improved high-temperature characteristics as compared with the Ti—Al alloys according to Comparative Examples.
The test results show that the Ti—Al alloys according to Embodiments are far superior to the Ti—Al alloys according to Comparative Examples in high-temperature characteristics as well as room-temperature characteristics. Further, as shown in
As shown in
In addition, the alloy of the present disclosure has a lamellar structure in which the α2 phases and the γ phases are arranged subsequently and regularly, the γ phase has a thickness of 100 nm to 200 nm, and the α2 phase has a thickness of 100 nm.
In contrast, in Comparative Examples, the α2 phases and the γ phases are irregularly arranged, and the γ phase has a thickness of 215 nm or 70.6 nm. This is outside a range of 100 nm to 200 nm which is a preferable γ-phase of the present disclosure.
Furthermore, in the alloys of Comparative Examples, the thickness ratio γ/α2 of the γ phase to the α2 phase is equal to 1.79 or less, and this is a value small than the thickness ratio γ/α2 of the γ phase to the α2 phase in the alloy of the present disclosure. Thus, in order to exhibit the aforementioned characteristics, the thickness ratio γ/α2 of the γ phase to the α2 phase is preferably equal to or more than 2.
While exemplary embodiments are described above, it is not intended that these embodiments describe all those possible. Rather, the words used in the specification are words of description rather than limitation, and it is understood that various changes may be made without departing from the spirit and scope of the disclosure.
Kim, Seong Woong, Na, Young Sang, Yeom, Jong Taek, Kim, Seung Eon
Patent | Priority | Assignee | Title |
Patent | Priority | Assignee | Title |
4294615, | Jul 25 1979 | United Technologies Corporation | Titanium alloys of the TiAl type |
4842819, | Dec 28 1987 | General Electric Company | Chromium-modified titanium aluminum alloys and method of preparation |
4842820, | Dec 28 1987 | General Electric Company | Boron-modified titanium aluminum alloys and method of preparation |
4879092, | Jun 03 1988 | General Electric Company | Titanium aluminum alloys modified by chromium and niobium and method of preparation |
5296056, | Oct 26 1992 | Rolls-Royce Corporation | Titanium aluminide alloys |
5653828, | Oct 26 1995 | National Research Council of Canada | Method to procuce fine-grained lamellar microstructures in gamma titanium aluminides |
5908516, | Aug 28 1996 | Titanium Aluminide alloys containing Boron, Chromium, Silicon and Tungsten | |
20040045644, | |||
20040071585, | |||
20100252146, | |||
H1988, | |||
JP10193087, | |||
JP10220236, | |||
KR101261885, |
Executed on | Assignor | Assignee | Conveyance | Frame | Reel | Doc |
Nov 18 2013 | YEOM, JONG TAEK | Korea Institute Of Machinery & Materials | ASSIGNMENT OF ASSIGNORS INTEREST SEE DOCUMENT FOR DETAILS | 031686 | /0308 | |
Nov 19 2013 | KIM, SEONG WOONG | Korea Institute Of Machinery & Materials | ASSIGNMENT OF ASSIGNORS INTEREST SEE DOCUMENT FOR DETAILS | 031686 | /0308 | |
Nov 19 2013 | KIM, SEUNG EON | Korea Institute Of Machinery & Materials | ASSIGNMENT OF ASSIGNORS INTEREST SEE DOCUMENT FOR DETAILS | 031686 | /0308 | |
Nov 19 2013 | NA, YOUNG SANG | Korea Institute Of Machinery & Materials | ASSIGNMENT OF ASSIGNORS INTEREST SEE DOCUMENT FOR DETAILS | 031686 | /0308 | |
Nov 27 2013 | Korea Institute Of Machinery & Materials | (assignment on the face of the patent) | / | |||
Jan 20 2020 | Korea Institute Of Machinery & Materials | KOREA INSTITUTE OF MATERIALS SCIENCE | ASSIGNMENT OF ASSIGNORS INTEREST SEE DOCUMENT FOR DETAILS | 055137 | /0489 |
Date | Maintenance Fee Events |
Mar 31 2021 | M2551: Payment of Maintenance Fee, 4th Yr, Small Entity. |
Date | Maintenance Schedule |
Oct 17 2020 | 4 years fee payment window open |
Apr 17 2021 | 6 months grace period start (w surcharge) |
Oct 17 2021 | patent expiry (for year 4) |
Oct 17 2023 | 2 years to revive unintentionally abandoned end. (for year 4) |
Oct 17 2024 | 8 years fee payment window open |
Apr 17 2025 | 6 months grace period start (w surcharge) |
Oct 17 2025 | patent expiry (for year 8) |
Oct 17 2027 | 2 years to revive unintentionally abandoned end. (for year 8) |
Oct 17 2028 | 12 years fee payment window open |
Apr 17 2029 | 6 months grace period start (w surcharge) |
Oct 17 2029 | patent expiry (for year 12) |
Oct 17 2031 | 2 years to revive unintentionally abandoned end. (for year 12) |